Method of producing high quality relaxed silicon germanium layers

ABSTRACT

A method for minimizing particle generation during deposition of a graded Si 1−x Ge x  layer on a semiconductor material includes providing a substrate in an atmosphere including a Si precursor and a Ge precursor, wherein the Ge precursor has a decomposition temperature greater than germane, and depositing the graded Si 1−x Ge x  layer having a final Ge content of greater than about 0.15 and a particle density of less than about 0.3 particles/cm 2  on the substrate.

PRIORITY INFORMATION

This application is a continuation of U.S. patent application Ser. No. 10/392,338, filed Mar. 19, 2003, now U.S. Pat. No. 7,041,170, which is a continuation-in-part of U.S. patent application Ser. No. 09/665,139, filed Sep. 19, 2000 now abandoned and entitled “Method of Producing Relaxed Silicon Germanium Layers,” which claims priority to and benefit of U.S. provisional application Ser. No. 60,154,851, filed Sep. 20, 1999. The entire disclosures of these applications are incorporated by reference herein.

TECHNICAL FIELD

This invention relates generally to producing silicon germanium layers and more particularly to producing high quality silicon germanium layers.

BACKGROUND OF THE INVENTION

Conventional techniques for producing relaxed silicon germanium (SiGe) layers on Si substrates typically consist of flowing germane (GeH₄) and a silicon precursor, such as silane (SiH₄) or dichlorosilane (SiH₂Cl₂), across a hot semiconductor substrate. When the temperature of these precursors reaches their respective decomposition temperatures, the precursors break down and Si and Ge atoms are free to deposit on the heated substrate. If the substrate is maintained at a sufficiently high temperature, thin-film crystal growth proceeds.

Commercialization of this method to produce relaxed SiGe layers on semiconductor substrates for use in optoelectronic and electronic devices demands an economical process of forming high quality SiGe layers. This means that production costs, such as equipment costs and production time must be minimized, while at the same time, the material properties of the SiGe layers produced must be tailored or optimized for their specific purpose.

Under most conditions, chemical vapor deposition (CVD) processes provide the most economical method of depositing thin layers of crystalline semiconductors. For example, in general, CVD equipment costs are much lower than corresponding equipment costs required to produce the same thin layer product using molecular beam epitaxy (MBE) techniques. Further, high thin-film growth rates can be achieved using CVD. These high growth rates (i.e. greater than 0.1 microns/minute) are essential in producing economical relaxed SiGe materials, since high growth rates reduce deposition time, thereby maximizing production rate and lowering the cost of the product.

While it is important to keep production costs low, it is equally important to produce high quality SiGe layers that possess the appropriate material properties for use in optoelectronic and electronic devices. High quality SiGe films have a low particle defect density (i.e. less than 0.3 particles/cm²) and a low threading dislocation density (i.e. less than 10⁶/cm²). If the produced SiGe layers do not achieve this level of quality, the electronic properties of the layers will not be suitable for use in optoelectronic and electronic devices.

Therefore, commercial production of high quality relaxed SiGe layers depends on the following three criteria:

-   -   A high growth rate is needed so that deposition time is         minimized and production rate is maximized, thereby reducing         costs of producing SiGe layers. An increase in growth rate is         typically achieved by increasing the substrate temperature and         precursor gas concentration.     -   The deposited SiGe layer has a low threading dislocation         density, so that the deposited SiGe layer is of high quality. A         decrease in threading dislocation density is typically achieved         by increasing the deposition temperature.     -   The deposited SiGe layer has a low particle defect density to         produce a high quality SiGe layer. A major source of particle         defects during epitaxial deposition is flaking of deposits on a         reactor wall. Therefore a decrease in reactor wall coating         buildup generally decreases the number of particles that         subsequently deposit on the SiGe layers.

One of the problems encountered when trying to extend conventional research methods of producing SiGe layers to a commercially viable process is that efforts to increase the growth rate and decrease the threading dislocation density also increase the particle defect density. This occurs because an increase in deposition temperature and an increase in precursor concentration leads to particle defects nucleating and depositing on the substrates and to an increase in coating buildup on the reactor walls, which eventually leads to flaking of the coating during growth of the SiGe layers.

This problem is exacerbated by the use of germane gas as a precursor. Germane decomposes at a much lower temperature, 675° C., than its silicon precursor counterpart (i.e. 900° C. for silane gas and 950° C. for dichlorosilane). Thus, any increase in deposition temperature increases the amount of Ge atoms available for deposition and thus increases deposits on reactor walls and particle defects on the substrate. The result of high temperature growth with germane is the formation of a brown or black, partially opaque coating on an inner surface of the reactor. In the case of a typical lamp-heated production CVD reactor, this coating limits the transmission of radiated energy from the lamps through the quartz reactor wall to the substrate. The loss of transmissivity of the reactor, which is typically a quartz tube, causes the inner surface of the reactor to heat to a temperature above 700° C., resulting in further deposits. Eventually, if left unchecked, the temperature of the reactor wall will reach 1000° C., at which point devitrification occurs. Both the reactor coating and devitrification can flake from the reactor walls and deposit on the substrate.

Most applications for relaxed Si_(1−x)Ge_(x) layers require an atomic Ge content above about 15% (x=0.15). In order to increase the Ge content in the layer, the precursor concentration of germane must be increased, thereby increasing particle defect generation.

Thus, it would be desirable to develop a method of producing relaxed SiGe layers on a semiconductor substrate that minimizes particle defect generation during deposition of SiGe layers, especially for high-Ge-content SiGe layers.

SUMMARY OF THE INVENTION

One solution to this problem is to change the gas chemistry such that deposition on the reactor walls is reduced, especially when producing Si_(1−x)Ge_(x) layers having a x value greater than 0.15. Thus, it is desirable to use a germanium precursor that decomposes at higher temperature.

Since the main problem in SiGe film growth is the low decomposition temperature of the germane gas, the present invention uses a germanium precursor having a higher decomposition temperature than germane, such as a germanium-halide. In this way, the decomposition temperatures of the precursors can be optimally chosen such that very high growth rates can be achieved at high growth temperatures, yet excessive reactor coating and particle defect introduction can be kept to a minimum.

Germanium halides include germanium-chlorine-containing species such as GeCl₄, or GeHCl₃, or GeH₂Cl₂, germanium-fluorine containing species, such as GeF₄, as well as germanium-bromine-containing species, such as GeBr₄, germanium-iodine-containing species, such as GeI₄, and germanium-astatine containing species, such as GeAt₄. In addition, any other combinations of these halides with germanium, such as GeClBr₃ or more generally a germanium-halide(1)_(x)-halide(2)_(y), where x+y=4 that have a higher decomposition temperature than germane may be used as a germanium precursor. These precursors can, unlike germane, be used at growth temperatures in excess of 800° C. to grow thick, relaxed SiGe layers without excessive reactor wall coating and particle defect formation. They can be utilized in gaseous form or in liquid form. In the case of a liquid precursor, a hydrogen carrier gas is typically bubbled through the liquid, and vapor from the liquid is carried into the reactor. Thus, typically the precursor will be in gaseous form inside the reactor. The germanium halide precursors can be combined with any of the typical silicon precursors, such as SiH₄, SiH₂Cl₂, SiHCl₃, SiHCl₄. Another advantage of this approach is that higher growth temperatures lead to lower threading dislocation densities in the relaxed graded layer. Thus, incorporating a different precursor for germanium leads to a lower defect density in the relaxed SiGe layers.

In general, in one aspect, the invention features a method for minimizing particle defect generation during deposition of a graded Si_(1−x)Ge_(x) layer on a semiconductor material. The method includes providing a substrate in an atmosphere including a Si precursor and a Ge precursor, wherein the Ge precursor has a higher decomposition temperature than germane (e.g., a germanium halide), and depositing a graded Si_(1−x)Ge_(x) layer having a final Ge content of greater than about 0.15 and a particle density of less than about 0.3 particles/cm² on the substrate.

Embodiments of this aspect of the invention include depositing the graded Si_(1−x)Ge_(x) layer at a temperature greater than about 600° C. In some embodiments, the Si_(1−x)Ge_(x) layer is deposited at a temperature greater than 800° C. In still yet other embodiments, the Si_(1−x)Ge_(x) layer is deposited at a temperature greater than 1000° C., and is preferably deposited at a temperature of 1100° C. In other embodiments, the graded Si_(1−x)Ge_(x) layer has a final Ge content of greater than 0.2, i.e. x>0.2. In another embodiment, the final Ge content is substantially equal to 1.0. The deposited Si_(1−x)Ge_(x) layers formed using the above method are grown with a deposition rate in excess of 0.3 microns/minute and under certain growth conditions, the deposition rate can exceed 3.0 microns/minute. In another embodiment, a low energy plasma, such as that produced by a direct current (DC) arc discharge is utilized in the reactor to enhance the reaction kinetics and hence the growth rate of the Si_(1−x)Ge_(x) layer. Gases such as Ar or H₂ can be used to facilitate the low energy plasma discharge. Low energy plasma rectors useful in carrying out the present invention include the CLUSTERLINE® LEP, manufactured by Unaxis, having corporate headquarters in Pfäffikon, Switzerland.

In another aspect, the invention features a method for minimizing particle defect generation during deposition of a graded Si_(1−x)Ge_(x) layer on a semiconductor material, wherein the reverse of the deposition or etching reaction removes unwanted deposits from the reactor chamber walls while the decomposition is in progress. The method includes providing a substrate in an atmosphere comprising a Si precursor, a Ge precursor, and an etchant gas. Removal of unwanted deposits on the reactor walls occurs because the halide etchant species (e.g., HCl produced from the decomposition of GeCl₄) is introduced as a byproduct of the decomposition of the silicon or germanium halide species. In addition, the hydrogen halides produce much higher etch rates than hydrogen species alone. Alternatively, the etchant gas (e.g., HCl, HBr, HF, or HI or a halide alone Cl₂, Br₂, F₂, or I₂) can be co-injected or introduced (i.e. etchant gas is present during at least some part of SiGe deposition) to reduce the accumulation of unwanted deposits on the reactor chamber walls.

In another aspect, the invention features a semiconductor material formed using the method as described above. The semiconductor material can be commercially produced because it is formed at high temperatures and deposition rates and because the material is of high quality, that is it has a defect level of less than about 0.3 particles/cm² and has a threading dislocation density of less than about 1×10⁶/cm².

In another aspect, the invention features a method including the steps of providing a substrate in an atmosphere of SiH₂Cl₂ and GeCl₄ and depositing a Si_(1−x)Ge_(x) layer on the substrate. The deposited Si_(1−x)Ge_(x) layer has a x value greater than or equal to 0.02 and a particle density of less than about 0.3 particles/cm².

BRIEF DESCRIPTION OF THE DRAWINGS

The invention, in accordance with preferred and exemplary embodiments, together with further advantages thereof, is more particularly described in the following detailed description, taken in conjunction with the accompanying drawings.

In the drawings, like reference characters generally refer to the same parts throughout the different views. Also, the drawings are not necessarily to scale, emphasis instead generally being placed upon illustrating principles of the invention.

FIG. 1 shows an Arrhenius plot of silicon growth rate versus temperature for SiH₄, SiH₂Cl₂, SiHCl₃, and SiCl₄.

FIG. 2 a shows an Arrhenius plot of normalized germanium growth rate in SiGe versus temperature for GeH₄.

FIG. 2 b shows a graph of calculated Gibbs free energy of reaction versus temperature for several Si and Ge precursors.

FIG. 2 c shows a table of decomposition temperatures for several silicon precursors and germanium precursors.

FIG. 3 shows a schematic view of one embodiment of a reactor used for producing relaxed SiGe layers in accordance with the present invention.

FIG. 4 shows a flow chart of an embodiment of a method for minimizing particle generation during deposition of a graded Si_(1−x)Ge_(x) layer.

FIG. 5 a shows a graph of growth rate of SiGe deposited in a research reactor versus mass ratio of GeCl₄ to SiH₂Cl₂ at 1000° C., 75 torr, and 100 sccm of SiH₂Cl₂.

FIG. 5 b shows a graph of atomic fraction of Ge in SiGe grown in the research reactor versus mass ratio of GeCl₄ to SiH₂Cl₂ at 1000° C., 75 torr, and 100 sccm of SiH₂Cl₂.

FIG. 6 a shows a cross-sectional view of a substrate including a graded Si_(1−x)Ge_(x) layer formed in accordance with the invention. Disposed on top of the graded Si_(1−x)Ge_(x) layer is a relaxed SiGe cap layer.

FIG. 6 b shows a cross-sectional view of a substrate including a graded Si_(1−x)Ge_(x) layer formed in accordance with the invention. Disposed on top of the graded Si_(1−x)Ge_(x) layer is a relaxed SiGe layer, and a thin, strained semiconductor layer of Ge.

FIG. 7 shows a table of achievable Si growth rates and achievable Si_(0.8)Ge_(0.2) growth rates when GeCl₄ is used for the Ge precursor.

FIG. 8 shows a flow chart of an embodiment of a method for minimizing particle generation during deposition of a semiconductor material.

DETAILED DESCRIPTION OF THE INVENTION

FIG. 1 is a graph showing the growth rate of silicon versus temperature for various silicon precursors, SiH₄ 102, SiH₂Cl₂ 104, SiHCl₃ 106, and SiCl₄ 108. Two distinct growth regimes are evident. For low temperatures, the growth rate has an exponential dependence on temperature, indicating that the growth is reaction rate or kinetically limited. For high temperatures, the growth rate has a weak dependence on temperature, indicating that the growth is mass-transport or diffusion-limited. Epitaxial layers are typically formed in the mass-transport limited-regime to minimize the effects of temperature variations during growth.

In between the two distinct growth regimes shown in FIG. 1 is a transition point 110. The temperature corresponding to the transition point for each precursor 102, 104, 106, and 108 is the decomposition temperature, or the temperature at which the precursor is nearly completely decomposed.

It is well known that as more hydrogen atoms in the SiH₄ molecule are replaced with chlorine atoms, the decomposition temperature of the precursor increases. This effect is reflected in the shift of the reaction-limited regime to higher temperatures for precursors with increasing chlorine content. For example, the mass-transport-limited growth regime of SiCl₄ 108 is shifted over 200° C. toward a higher temperature compared to that of SiH₄ 102. As a result, epitaxial films can be grown with SiCl₄ at much higher temperatures than with SiH₄ while avoiding the effects of particle defect formation and reactor wall coating. Additionally, extremely high growth rates can be achieved at higher temperatures using these chlorine-based precursor chemistries.

It is also known for silicon precursors that as the pressure at which deposition is carried out is changed from atmospheric to reduced pressure, chamber coating tends to increase. This is supported by the chemical equations for decomposition reactions, which have a larger number of moles of gaseous product than of reactants. This characteristic of the decomposition reactions (larger volume of reactants than products) favors the forward reaction, i.e. formation reaction, at lower pressure. Thus the decomposition temperature of the precursors will generally be lower at reduced pressures, a characteristic that can be extended to the germanium precursors as well. For this reason, atmospheric pressure deposition may be preferred to reduce chamber coating.

Since the main problem with conventional techniques of depositing SiGe layers is the low decomposition temperature of the germane gas, the present invention uses any germanium precursor that has a higher decomposition temperature than germane, such as a germanium-halide precursor. As in the silicon system, chlorogermanes and other germanium halides can be used to extend growth temperatures to more than 200° C. over germane, GeH₄, growth temperatures without increasing particle defect deposition.

FIG. 2 a shows a graph of temperature versus normalized growth rate of Ge in SiGe for a conventional Ge precursor, GeH₄ 202. Using FIG. 2 a, FIG. 2 b, a graph of calculated Gibbs free energy of reaction versus temperature for several Si and Ge precursors, and FIG. 1, which shows that the decomposition temperature increases with increasing the chlorine (halide) content, it is expected that the decomposition temperature of any germanium halide precursor will be significantly higher than germane, GeH₄. For example, FIG. 1 shows that the decomposition temperature, the temperature corresponding to the transition point 110, of SiH₄ 102 is 900° C., the decomposition temperature for SiH₂Cl₂ 104 is 950° C., and the decomposition temperature of SiCl₄ 108 is 1150° C. FIG. 2 b shows that the calculated Gibbs free energy curve for SiCl₄ 204 is greater than a calculated Gibbs free energy curve for SiH₂Cl₂ 206, which is greater than a calculated Gibbs free energy curve for SiH₄ 208. Thus, it is expected that Ge precursors will follow the same trends as the Si precursors and that Ge precursors that have a calculated Gibbs free energy curve that is greater than the calculated Gibbs free energy curve for GeH₄ will also have a greater decomposition temperature than GeH₄.

As shown in FIG. 2 a, germane, GeH₄ 210, has the lowest Gibbs free energy of reaction indicating that it decomposes at the lowest temperature of all of the Ge precursors shown. GeCl₄ 212, GeBr₄ 214, GeF₄ 216, and GeI₄ 218 have much higher decomposition temperatures than GeH₄ 210. Thus, when high purity sources of these germanium halides are used as the Ge precursor, SiGe growth can occur with minimal reactor coating at temperatures above 600° C. In this way, the decomposition temperatures of precursors can be optimally chosen such that very high growth rates can be achieved at high temperatures. For example, selecting a Si precursor and a Ge precursor that both have a decomposition temperature above about 900° C. can minimize particle defect generation. If both selected Si and Ge precursor gases decompose at about the same high temperature then most of the free Si and Ge atoms should react and form epitaxial Si_(1−x)Ge_(x) layers on the heated substrate. Otherwise, if the decomposition temperatures of the selected precursors are not within the same range, i.e. ±200° C., then the free atoms of the precursor that decomposes at a lower temperature will begin to rapidly deposit on surfaces, such as reactor walls and substrates, as particle defects prior to the decomposition of the other precursor.

FIG. 2 c illustrates estimated decomposition temperatures for various Si precursors and Ge precursors. The most readily available germanium halide precursor is germanium tetrachloride, GeCl₄. This precursor, unlike germane, GeH₄, can be used at growth temperatures in excess of 800° C. to grow thick, relaxed Si_(1−x)Ge_(x) layers without excessive reactor coating and particle defect formation. It can be combined with any of the Si precursors, such as SiH₄, SiH₂Cl₂, SiHCl₃, and SiCl₄ to form high quality SiGe layers. However, it is noted that in a preferred embodiment of the invention a combination of SiH₂Cl₂ and GeCl₄ is used, since the decomposition temperatures for these gases are within 25° C. of each other.

In the present invention, a CVD reactor 300, as shown in FIG. 3, is used to produce the relaxed SiGe layers on semiconductor substrates. The CVD reactor 300 includes a quartz tube 302, a heat source 304, a precursor gas inlet 306, a susceptor 308, and in some embodiments a vacuum pump 310 (shown in phantom view). To produce relaxed SiGe layers on a semiconductor material, a silicon substrate 311 is positioned on the susceptor 308. Next, the vacuum pump can be activated to continuously evacuate the gasses within the quartz tube 302 and to maintain a constant pressure (760 torr to 0.010 torr) within the reactor 300 during deposition. Then the heat source 304, which typically comprises multiple tungsten-halogen lamps, is activated so that the temperature of the Si substrate is increased to deposition temperature (600° C.-1200° C.). Once the Si substrate 311 has reached the specified deposition temperature, a Si precursor 312 and a Ge precursor 314 having a decomposition temperature greater than germane (e.g., a germanium halide precursor) enter the reactor 300 through the gas inlet 306. The concentration of the precursors is typically controlled through mass-flow controllers connected to the precursor tanks. These precursors 312, 314 flow over the heated silicon substrate 311 and deposit thereon. A Ge content, x, of the Si_(1−x)Ge_(x) layer is controlled by the relative concentration of the Si and Ge precursors. In some embodiments, a SiGe layer having a uniform content of Ge throughout is deposited on the silicon substrate. For example, a layer of material having a uniform concentration of Si_(0.98)Ge_(0.02) can be deposited on the Si substrate 311. In other embodiments, multiple Si_(1−x)Ge_(x) layers each having a successively greater Ge, x, content may be deposited on the silicon substrate to form a graded layer. Alternatively, the graded layer Ge content profile may be substantially linear (i.e. no individual layers are evident within the profile.) By increasing the Ge content gradually, the strain due to lattice mismatch between Si and Ge is relieved, thereby minimizing threading dislocation density in the deposited relaxed SiGe layer. Typically, the Ge content of the graded Si_(1−x)Ge_(x) layer is increased at a rate of less than about 25% Ge per micron. However, in some embodiments the increase may be greater than 25% Ge per micron. In either embodiment, due to the high processing temperatures available in the present invention, the density of threading dislocation intersecting the top surface of the Si_(1−x)Ge_(x) layer is less than about 1×10⁶/cm².

For graded Si_(1−x)Ge_(x) layers deposited using this method, a final Ge content, i.e. the Ge content of the final layer deposited, will exceed 15% and in some embodiments the final Ge content will exceed 20%. In other embodiments, the Ge content may approach 100%.

FIG. 4 shows a flow chart of one embodiment of the method of the invention. Specifically, a method 400 for minimizing particle generation particle generation during deposition of a graded Si_(1−x)Ge_(x) layer on a semiconductor material within a reactor, such as the reactor 300 shown in FIG. 3, includes at least two steps. First, as shown in step 402, a substrate is placed within an atmosphere including both a Si precursor and a Ge precursor. The Ge precursor is any germanium source that has a decomposition temperature higher than that of germane. In general, germanium halides, such as, for example, GeCl₄, GeHCl₃, GeH₂Cl₂, GeBr₄, GeI₄, GeF₄, and GeAt₄, have a decomposition temperature higher than the decomposition temperature of germane. The Si precursor is typically selected from the group consisting of SiHCl₃, SiH₂Cl₂, SiCl₄, and SiH₄. However, any Si-based precursor that has a decomposition temperature above about 700° C. may be selected as a Si precursor, possibly including other silicon-halide compounds.

Next, as shown in step 404, a graded Si_(1−x)Ge_(x) layer having a final Ge content of greater than about 15% (i.e. x>0.15) and a particle defect density less than about 0.3 particles/cm² is deposited on the substrate. The low particle defect density and high final Ge content of the Si_(1−x)Ge_(x) layer results because the method 400 takes advantage of using a germanium halide for the Ge precursor and matching the decomposition temperature of the selected germanium halide to a particular Si precursor. For example, with reference to FIGS. 1 and 2, the graded Si_(1−x)Ge_(x) layer may be deposited in reactor 300 using a combination of SiH₄ and GeH₂Cl₂ at a temperature above about 600° C., and more preferably at a temperature above about 800° C. At these temperatures, a low energy plasma can be used to aid the cracking of the precursors and to give higher growth rates at a lower temperature.

In another embodiment of the graded Si_(1−x)Ge_(x) layer, the selected Si and Ge precursors are SiH₂Cl₂ and GeCl₄. In this embodiment, the deposition occurs at a temperature greater than about 1000° C., and preferably at a temperature between 1050° C. and 1100° C. The SiH₂Cl₂ is introduced into the reactor 300 at a constant flow rate of about 100 sccm or greater. The GeCl₄ is introduced into the reactor using a hydrogen carrier gas at an incremental flow rate increased from 0 to 250 sccm to produce a graded Si_(1−x)Ge_(x) layer having a final Ge content of about 20%, i.e. x=0.2. In some embodiments the GeCl₄ is introduced into the reactor using a hydrogen carrier gas at an incremental flow rate increased from 0 to 350 sccm to produce a graded Si_(1−x)Ge_(x) layer having a final Ge content of about 30%, i.e. x=0.3.

In another embodiment, the deposition process is performed at atmospheric pressure for the purpose of reducing reactor chamber wall deposits to a lower level. This is done to take advantage of the reduced tendency of the silicon and germanium precursors to decompose at higher pressure.

Referring to FIGS. 5 a and 5 b, experimentation in a research reactor system at 1000° C. and 75 torr, shows that the growth rate of the SiGe layer increases with increasing a mass ratio of GeCl₄ to SiH₂Cl₂ to a growth rate of about 0.25 microns/minute with a Ge atomic fraction of about 0.3. Since state of the art reactor systems typically achieve greater growth rates than research reactor systems, it is believed that deposition of SiGe layers from SiH₂Cl₂ and GeCl₄ at this temperature (1000° C.), pressure (75 torr) in a state of the art reactor system will be at a growth rate greater than 0.25 microns/minute.

FIG. 6 a shows a cross-sectional view of the silicon substrate 311 including a graded Si_(1−x)Ge_(x) layer 520 formed in accordance with the invention. Disposed on top of the graded Si_(1−x)Ge_(x) layer 520 is a substantially relaxed Si_(1−y)Ge_(y) layer 522. The layer 522 shown in this embodiment has a Ge content, y, that is approximately equal to the final Ge content of the graded Si_(1−x)Ge_(x) layer. Generally, the relaxed Si_(1−x)Ge_(x) layers and the Si_(1−y)Ge_(y) layers produced in accordance with the invention are smooth and have a surface roughness of less than 5 nm for a 40×40 micron atomic force microscopy scan. In an additional embodiment, shown in FIG. 6 b, a thin, strained semiconductor 524 layer of Ge may be disposed above the substantially relaxed Si_(1−y)Ge_(y) layer. Alternatively, this layer 524 may be formed from Si or SiGe.

The ability to deposit films at high temperatures using a germanium halide gas, such as GeCl₄, results in a lower particle defect density within the deposited relaxed Si_(1−x)Ge_(x) layer than for Si_(1−x)Ge_(x) layers formed at the same temperatures using conventional methods. For example, relaxed Si_(1−x)Ge_(x) layers formed in accordance with the present invention and at a temperature of about 1000° C. have a particle defect level of less than about 0.3 particles/cm², whereas Si_(1−x)Ge_(x) layers formed using conventional research techniques (i.e. GeH₄ gas used and a final Ge content below about 15%) have a particle defect density of 0.6 to 2 particles/cm², or higher. Further, relaxed Si_(1−x)Ge_(x) layers produced in accordance with the present invention typically have a localized light-scattering defect level of less than about 0.3 defects/cm² for particle defects having a size (diameter) greater than 0.13 microns, a defect level of about 0.2 defects/cm² for particle defects having a size greater than 0.16 microns, a defect level of about 0.1 defects/cm² for particle defects having a size greater than 0.2 microns, and a defect level of about 0.03 defects/cm² for defects having a size greater than 1 micron. It is believed that process optimization will enable reduction of the localized light-scattering defect levels to about 0.09 defects/cm² for particle defects having a size greater than 0.09 microns and to 0.05 defects/cm² for particle defects having a size greater than 0.12 microns.

Thus, by using a Ge precursor with a decomposition temperature higher than that of germane (e.g., a germanium halide precursor), Si_(1−x)Ge_(x) layers may be produced at higher temperatures while maintaining a high quality level, i.e. particle defect density less than 0.3 particle defects/cm², even at high Ge contents, e.g., x>0.15. Moreover, since deposition can occur at temperatures above 1000° C., growth rates greater than 0.1 microns/minute are achievable. For example, FIG. 7 shows a table of achievable Si growth rates and corresponding estimated achievable Si_(0.8)Ge_(0.2) growth rates for deposition processes using GeCl₄ and various silicon precursors. The estimated achievable SiGe growth rates are calculated using the lower value calculated from the following two equations, in which R is the growth rate and F is the atomic fraction: R _(SiGe) ≈F _(Ge) *R _(Ge) +F _(Si) *R _(Si)   Equation 1 R _(SiGe) ≈R _(Ge) /F _(Ge)   Equation 2 Reported values of the growth rate for Si (R_(Si)) for various Si precursors is shown in the second column of FIG. 7. The growth rate (R_(Ge)) of GeCl₄ is estimated to be 0.75 microns/minute, a value based on a comparison of the decomposition temperature and resulting growth rates for SiH₄ and SiH₂Cl₂. As shown in FIG. 7, an achievable growth rate for the combination of SiH₂Cl₂ and GeCl₄ is 1.1 micron/minute and is 3.8 microns/minute for the combination of SiHCl₃ and GeCl₄. Both of these achievable growth rates allow production times to be drastically cut.

Production time in the present invention is further reduced due to the decrease in particles depositing and coating the reactor walls. Typically, once the coating on the reactor 300 reaches a thickness greater than 1 micron, the transmissivity of the quartz tube 302 will deteriorate quickly, resulting in an increase in temperature and ultimately in devitrification. To prevent contaminants from flaking off of the quartz tube 302 and landing on the depositing Si_(1−x)Ge_(x) layers 520, the quartz tube 302 is cleaned to remove the coating once the coating reaches a thickness of 1 micron or more. Since the invention limits the amount of reactor coating by increasing the decomposition temperature of the Ge precursor (germanium halide) to near that of the Si precursor, the coating takes longer to grow on the walls, e.g., 175 hours of deposition time, and thus less time is lost to cleaning the quartz tube 302. An additional source of coating minimization may arise from etching action arising from the halogen component of the Ge precursor.

Because hydrogen-halide and halide gases etch silicon at a significantly higher rate than hydrogen, these gases (primarily HCl) are typically used to etch coatings from quartz reactor walls. In the same way, halogen-containing byproducts of the SiGe deposition will aid this etching action. Thus in another aspect of this invention, the etching reduces the accumulation of unwanted deposits on the quartz walls while deposition is being done in the reactor. This can occur because the halide etchant species (e.g., HCl produced from the decomposition of GeCl₄) is introduced as a byproduct of the decomposition of the silicon or germanium halide species. In another embodiment of this invention, the etchant gas (e.g., HCl, HBr, HF, or HI or a halide alone Cl₂, Br₂, F₂, or I₂) can be co-injected or introduced to reduce the accumulation of unwanted deposits on the reactor chamber walls, i.e., the quartz tube 302. For example, HCl can be co-injected into the reactor along with the Si and Ge precursors at a flow rate of less than or equal to 2 slm (standard liters per minute). In a preferred embodiment, HCl is co-injected into the reactor at a rate of less than or equal to 0.5 slm. Also, co-injection of the etchant gas can even be used to reduce reactor wall deposits when germane gas is used as the Ge precursor because the etchant gas, which includes a halide source, can reduce the accumulation of unwanted deposits at a higher rate than hydrogen. Co-injection can be more effective at introducing the etchant gas to the walls of the reactor than by introducing the etchant gas by reaction of the Si and Ge precursors, because delivery of the co-injected gases can be controlled. If the etchant gas is produced solely as a byproduct of deposition, it must diffuse from the susceptor 308 to the walls of the reactor 302 to etch the deposits. One helpful aspect of this process is that the Gibbs free energy of the etching reactions is much less temperature dependent than the deposition process so that the etch rate at the walls stays high even though the temperature at the wall is significantly lower than the temperature at the susceptor 308.

The invention can be further optimized to produce the highest quality relaxed Si_(1−x)Ge_(x) layers. For example, in one embodiment, the susceptor 308 can be rotated during deposition to compensate for depletion of a precursor and to produce a uniform deposition of Si_(1−x)Ge_(x) over the entire substrate 311.

Referring to FIG. 8, our invention also provides a method 700 for depositing a Si_(1−x)Ge_(x) layer having a uniform Ge content and a low particle defect density. Specifically, method 700 includes two steps, 702 and 704. First, as according to step 702, a substrate is positioned within a reactor having an atmosphere of SiH₂Cl₂ and GeCl₄. Then, as shown in step 704, the Si_(1−x)Ge_(x) layer is deposited on the substrate. The deposited Si_(1−x)Ge_(x) layer has an x value of at least 0.02 and a particle defect density of less than about 0.3 particles/cm². The low particle defect density observed in Si_(1−x)Ge_(x) layers deposited using method 700 is a result of using Si and Ge precursors that have a decomposition temperatures above about 700° C. and that are optimally matched, i.e. have a decomposition temperatures within ±25° C. of each other.

Using method 700, a uniform Si_(1−x)Ge_(x) layer having a particle defect density of less than 0.3 particles/cm² can be deposited on substrates. For example, a Si_(0.98)Ge_(0.02) layer may be formed on a Si wafer by introducing SiH₂Cl₂ gas into reactor 300 at a flow rate of about 100 sccm and GeCl₄ gas within a hydrogen carrier gas at a constant flow rate of 25 sccm. The Si_(0.98)Ge_(0.02) layer deposits at a temperature above about 600° C., and preferably at a temperature of 1100° C.

While the invention has been particularly shown and described with reference to specific preferred embodiments, it should be understood by those skilled in the art that various changes in form and detail may be made therein without departing from the spirit and scope of the invention as defined by the appended claims. 

1. A method for minimizing particle generation during deposition of a graded Si_(1−x)Ge_(x) layer on a semiconductor material within a reactor, the method comprising the steps of: (a) providing a substrate in an atmosphere comprising a Si precursor and a Ge precursor, wherein the Ge precursor has a higher decomposition temperature than germane; and (b) depositing the graded Si_(1−x)Ge_(x) layer on the substrate, the Si_(1−x)Ge_(x) layer having a final Ge content wherein x is greater than about 0.15 and a particle density less than about 0.3 particles/cm².
 2. The method of claim 1 wherein the Ge precursor comprises a germanium halide.
 3. The method of claim 1 wherein the graded Si_(1−x)Ge_(x) layer is deposited at a temperature of greater than about 600° C.
 4. The method of claim 1 wherein the graded Si_(1−x)Ge_(x) layer is deposited at a temperature of greater than about 800° C.
 5. The method of claim 1 wherein the graded Si_(1−x)Ge_(x) layer is deposited at a temperature of greater than about 1000° C.
 6. The method of claim 1 wherein the graded Si_(1−x)Ge_(x) layer is deposited at a temperature of about 1100° C.
 7. The method of claim 1 wherein the final Ge content of the graded Si_(1−x)Ge_(x) layer has a value for x substantially equal to 1.0.
 8. The method of claim 1 further comprising providing a substantially relaxed Si_(1−y)Ge_(y) layer disposed above the graded Si_(1−x)Ge_(x) layer wherein y is approximately equal to the final Ge content of the graded Si_(1−x)Ge_(x) layer.
 9. The method of claim 8 further comprising providing a thin, strained semiconductor layer disposed above the graded Si_(1−y)Ge_(y) layer.
 10. The method of claim 9 wherein the thin, strained semiconductor layer is selected from the group consisting of Si, Ge, and SiGe.
 11. The method of claim 1 wherein the Ge content is increased at a rate less than about 25% per micron resulting in a density of threading dislocation intersecting the surface of the graded Si_(1−x)Ge_(x) layer of less than about 1×10⁶/cm².
 12. The method of claim 1 wherein the Ge content is increased at a rate greater than about 25% per micron resulting in a density of threading dislocation intersecting the surface of the graded Si_(1−x)Ge_(x) layer of less than about 1×10⁶/cm².
 13. The method of claim 1 wherein a deposition rate of the graded Si_(1−x)Ge_(x) layer is greater than about 0.3 microns per minute.
 14. The method of claim 1 wherein a deposition rate of the graded Si_(1−x)Ge_(x) layer is greater than about 1 micron per minute.
 15. The method of claim 1 wherein a deposition rate of the graded Si_(1−x)Ge_(x) layer is greater than about 3 micron per minute.
 16. The method of claim 2 wherein the Ge precursor is selected from the group consisting of GeCl₄, GeHCl₃, and GeH₂Cl₂.
 17. The method of claim 1 wherein the Si precursor is selected from the group consisting of SiH₂Cl₂, SiHCl₃, SiH₄, and SiCl₄.
 18. The method of claim 1 further comprising rotating the substrate during deposition of the graded Si_(1−x)Ge_(x) layer.
 19. The method of claim 1 further comprising depositing the graded Si_(1−x)Ge_(x) layer to include a surface roughness of less than about 5 nm for a 40×40 micron scan.
 20. The method of claim 1 further comprising depositing the graded Si_(1−x)Ge_(x) layer at a pressure between about 760 torr and about 0.010 torr.
 21. The method of claim 1 wherein step (b) comprises depositing the graded Si_(1−x)Ge_(x) layer on the substrate while preventing the deposition of a coating greater than about 1 micron thick on an inner surface of the reactor, the Si_(1−x)Ge_(x) layer having a final Ge content wherein x is greater than about 0.15 and a particle density of less than about 0.3 particles/cm².
 22. A method for minimizing particle generation during deposition of a graded Si_(1−x)Ge_(x) layer on a semiconductor material within a reactor, the method comprising the steps of: (a) providing a substrate in an atmosphere comprising a Si precursor, a Ge precursor, and an etchant gas, wherein the etchant gas includes a halide source and reduces accumulation of semiconductor deposits on reactor walls; and (b) depositing the graded Si_(1−x)Ge_(x) layer on the substrate, the Si_(1−x)Ge_(x) layer having a final Ge content wherein x is greater than about 0.15 and a particle density less than about 0.3 particles/cm².
 23. The method of claim 22 wherein the etchant gas is selected from the group consisting of HCl, HBr, HF, HI, Cl₂, Br₂, F₂, and I₂.
 24. A semiconductor material formed by the process of claim
 1. 25. The semiconductor material of claim 24 wherein the graded Si_(1−x)Ge_(x) layer has a localized light-scattering defect level of less than about 0.3 defects/cm², the particle defects having a size greater than about 0.13 microns.
 26. The semiconductor material of claim 24 wherein the graded Si_(1−x)Ge_(x) layer has a localized light-scattering defect level of less than about 0.2 defects/cm², the particle defects having a size greater than about 0.16 microns.
 27. The semiconductor material of claim 24 wherein the graded Si_(1−x)Ge_(x) layer has a localized light-scattering defect level of less than about 0.1 defects/cm², the particle defects having a size greater than about 0.2 microns.
 28. The semiconductor material of claim 24 wherein the graded Si_(1−x)Ge_(x) layer has a localized light-scattering defect level of less than about 0.03 defects/cm², the particle defects having a size greater than about 1 micron.
 29. The semiconductor material of claim 24 wherein each layer within the graded Si_(1−x)Ge_(x) layer has a substantially uniform composition across the substrate. 